Method for producing ga2o3 crystal film

ABSTRACT

A Ga 2 O 3  crystal film is epitaxially grown on a Ga 2 O 3  crystal substrate using an MBE method, while controlling the n-type conductivity with high accuracy. Provided is a method for producing a Ga 2 O 3  crystal film, wherein a conductive Ga 2 O 3  crystal film is formed by epitaxial growth using an MBE method. This method for producing a Ga 2 O 3  crystal film comprises a step wherein a Ga 2 O 3  single crystal film containing Sn is grown by producing a Ga vapor and an Sn vapor and supplying the Ga vapor and the Sn vapor to the surface of a Ga 2 O 3  crystal substrate as molecular beams The Sn vapor is produced by heating Sn oxide that is filled in a cell of an MBE apparatus.

TECHNICAL FIELD

The invention relates to a method for producing a Ga₂O₃ based crystal film.

BACKGROUND ART

A method of forming a conductive Ga₂O₃ crystal film on a crystal substrate such as sapphire substrate by heteroepitaxial growth is known as a conventional method for producing a Ga₂O₃ based crystal film (see e.g. PTL 1). PTL 1 discloses that a Ga₂O₃ crystal film is formed using an MBE method and Sn is used as a conductive impurity for imparting conductivity to the Ga₂O₃ crystal film.

CITATION LIST Patent Literature PTL 1

Japanese patent No. 4,083,396

SUMMARY OF INVENTION Technical Problem

It is an object of the invention to epitaxially grow a Ga₂O₃ based crystal film on a Ga₂O₃ based crystal substrate using an MBE method while controlling the n-type conductivity with high accuracy.

Solution to Problem

According to one embodiment of the invention, a method for producing a Ga₂O₃ based crystal film as defined in [1] to [3] below is provided so as to achieve the above object.

[1] A method for producing a Ga₂O₃ based crystal film using a MBE method to form a conductive Ga₂O₃ based crystal film by epitaxial growth, comprising a step of generating Ga vapor and Sn vapor and supplying the Ga vapor and the Sn vapor as a molecular beam to a surface of a Ga₂O₃ based crystal substrate so as to grow a Ga₂O₃ based single crystal film comprising Sn,

-   -   wherein the Sn vapor is generated by heating a Sn oxide that is         filled in a cell of an MBE apparatus.

[2] The method for producing a Ga₂O₃ based crystal film according to [1], wherein the Sn oxide comprises SnO₂, and

-   -   wherein the Sn vapor is generated at a temperature of the cell         of 650° C. to 925° C.

[3] The method for producing a Ga₂O₃ based crystal film according to [1] or [2], wherein the Ga₂O₃ single crystal is epitaxially grown at a growth rate of 0.01 to 100 μm/h.

[4] The method for producing a Ga₂O₃ based crystal film according to any one of [1] to [3], wherein a carrier concentration of the Ga₂O₃ based crystal film is 1×10¹⁴ to 1×10²⁰/cm³.

[5] The method for producing a Ga₂O₃ based crystal film according to [1], wherein the Sn oxide comprises SnO₂, and

-   -   wherein the Sn vapor is generated at a temperature of the cell         of 450° C. to 1080° C.

[6] The method for producing a Ga₂O₃ based crystal film according to [5], wherein the Ga₂O₃ single crystal is epitaxially grown at a growth rate of 0.01 to 100 μm/h.

[7] The method for producing a Ga₂O₃ based crystal film according to [5], wherein the Ga₂O₃ single crystal is epitaxially grown at a growth temperature of 530° C. to 600° C.

Advantageous Effects of Invention

According to one embodiment of the invention, a Ga₂O₃ based crystal film can be epitaxially grown on a Ga₂O₃ based crystal substrate using an MBE method while controlling the n-type conductivity with high accuracy.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a vertical cross sectional view showing a Ga₂O₃ based crystal substrate and a Ga₂O₃ based crystal film in an embodiment.

FIG. 2 shows a configuration example of an MBE apparatus used for forming the Ga₂O₃ based crystal film.

FIG. 3 is a graph showing a relation between temperature of a second cell filled with SnO₂ and a carrier concentration in the Ga₂O₃ based crystal film in Example 1.

FIG. 4 is a graph showing a relation between temperature of the second cell filled with SnO₂ and a carrier concentration in the Ga₂O₃ based crystal film in Example 1.

FIG. 5 is a graph showing a relation between temperature of the second cell filled with Si and a carrier concentration in the Ga₂O₃ based crystal film in Comparative Example.

FIG. 6 is a graph showing a relation between temperature of the second cell filled with SnO₂ and a donor concentration in the Ga₂O₃ based crystal film in Example 2.

FIG. 7 is a graph showing a relation between temperature of the second cell filled with SnO₂ and a donor concentration in the Ga₂O₃ based crystal film in Example 2.

DESCRIPTION OF EMBODIMENTS Embodiment

As a result of study and investigation, the present inventors found that conductivity is greatly affected by the type of raw material of conductive impurity for imparting conductivity to a Ga₂O₃ based crystal film when a conductive Ga₂O₃ based crystal film is epitaxially grown on a substrate formed of a Ga₂O₃ based crystal, and it is necessary to use a Sn oxide.

A Ga₂O₃ based crystal film formed on a Ga₂O₃ based crystal substrate by epitaxial growth can have higher quality than that formed on a substrate having a greatly different crystal structure by heteroepitaxial growth.

In the present embodiment, a highly-conductive Ga₂O₃ based crystal film is epitaxially grown and formed on a Ga₂O₃ based crystal substrate by the molecular beam epitaxy (MBE) method using an appropriately selected type of raw material of conductive impurity and heating temperature of the raw material. An example embodiment thereof will be described below.

(Ga₂O₃ Based Crystal Film)

FIG. 1 is a vertical cross sectional view showing a Ga₂O₃ based crystal substrate and a Ga₂O₃ based crystal film in the embodiment.

A Ga₂O₃ based crystal film 1 is formed by epitaxially growing a Ga₂O₃ based single crystal on a Ga₂O₃ based crystal substrate 2 using the MBE method. The MBE method is a crystal growth method in which a raw material used alone or as a compound is heated in an evaporation source called cell and vapor generated by heat is supplied as a molecular beam onto the surface of the substrate to epitaxially grow a crystal.

The Ga₂O₃ based crystal film 1 is formed of an n-type β-Ga₂O₃ single crystal containing Sn as a conductive impurity. Here, the β-Ga₂O₃ based single crystal means a β-Ga₂O₃ single crystal as well as a β-Ga₂O₃ single crystal in which a Ga site is substituted by Al, etc. (e.g., a β-(Al_(x)Ga_(1−x))₂O₃ single crystal (0<x<1)). The Ga₂O₃ based crystal film 1 has a thickness of, e.g., about 10 to 1000 nm.

The carrier concentration in the Ga₂O₃ based crystal film 1 is 1×10¹⁴ to 1×10²⁰/cm³. This carrier concentration can be controlled by temperature of a second cell 13 b of a below-described MBE apparatus 3 during film formation. The second cell 13 b is a cell filled with SnO₂ as a raw material of Sn which is an impurity for imparting conductivity to the Ga₂O₃ based crystal film 1.

The Ga₂O₃ based crystal substrate 2 is formed of a β-Ga₂O₃ s based ingle crystal of which resistance is increased by adding an impurity such as Mg.

The Ga₂O₃ based crystal substrate 2 is made by, e.g., the following procedure. Firstly, a semi-insulating β-Ga₂O₃ single crystal ingot doped with an impurity is made by the EFG method. As the impurity, it is possible to use, e.g., H, Li, Na, K, Rb, Cs, Fr, Be, Ca, Sr, Ba, Ra, Mn, Fe, Co, Ni, Pd, Cu, Ag, Au, Zn, Cd, Hg, Ti or Pb when substituting Ga site. Meanwhile, it is possible to use N or P when substituting oxygen site. For example, for doping Mg, MgO powder is mixed to raw material powder. Not less than 0.05 mol % of MgO is added to impart good insulation properties to the Ga₂O₃ based crystal substrate 2. Alternatively, the semi-insulating β-Ga₂O₃ single crystal ingot may be made by the FZ method. The obtained ingot is sliced to a thickness of, e.g., about 1 mm so that the principal surface has a desired plane orientation, thereby forming a substrate. Then, a grinding and polishing process is performed to a thickness of about 300 to 600 μm.

(Method for Producing Ga₂O₃ Based Crystal Film)

FIG. 2 shows an example configuration of an MBE apparatus used for forming the Ga₂O₃ based crystal film. A MBE apparatus 3 is provided with a vacuum chamber 10, a substrate holder 11 supported in the vacuum chamber 10 to hold the Ga₂O₃ based crystal substrate 2, heating devices 12 held on the substrate holder 11 to heat the Ga₂O₃ based crystal substrate 2, plural cells 13 (13 a, 13 b, 13 c) filled with raw materials of atoms constituting the Ga₂O₃ based crystal film 1, heaters 14 (14 a, 14 b, 14 c) for hearing the cells 13, a gas supply pipe 15 for supplying oxygen-based gas into the vacuum chamber 10, and a vacuum pump 16 for exhausting the air in the vacuum chamber 10. It is configured that the substrate holder 11 can be rotated by a non-illustrated motor via a shaft 110.

The first cell 13 a is filled with a Ga raw material of the Ga₂O₃ based crystal film 1, such as

Ga powder. The Ga powder desirably has a purity of not less than 6N. The second cell 13 b is filled with the Sn oxide (SnO₂ or SnO) powder which is a Sn raw material to be doped as a donor to the Ga₂O₃ based crystal film 1. The Sn oxide may not be in the form of powder. The third cell 13 c is filled with, e.g., an Al raw material which is used when the Ga₂O₃ based crystal film 1 is formed of a β-(Al_(x)Ga_(1−x))₂O₃ single crystal. A shutter is provided at an opening of each of the first cell 13 a, the second cell 13 b and the third cell 13 c.

Firstly, the preliminarily-formed Ga₂O₃ based crystal substrate 2 is attached to the substrate holder 11 of the MBE apparatus 3. Next, the vacuum pump 16 is activated to reduce atmospheric pressure in the vacuum chamber 10 to about 1×10⁻⁸ Pa. Then, the Ga₂O₃ based crystal substrate 2 is heated by the heating devices 12. Here, radiation heat of heat source such as graphite heater of the heating device 12 is thermally transferred to the Ga₂O₃ based crystal substrate 2 via the substrate holder 11 and the Ga₂O₃ based crystal substrate 2 is thereby heated.

After the Ga₂O₃ based crystal substrate 2 is heated to a predetermined temperature, oxygen-based gas such as oxygen radical is supplied into the vacuum chamber 10 through the gas supply pipe 15. Partial pressure of the oxygen-based gas is, e.g., 5×10⁻⁴ Pa.

After a period of time required for stabilization of gas pressure in the vacuum chamber 10 (e.g., after 5 minutes), the first cell 13 a, the second cell 13 b and, if necessary, the third cell 13 c are heated by the first heater 14 a while rotating the substrate holder 11 so that Ga, Sn and Al are evaporated and are radiated as molecular beam onto the surface of the Ga₂O₃ based crystal substrate 2.

For example, the first cell 13 a is heated to 900° C. and beam-equivalent pressure (BEP) of Ga vapor is 2×10⁻⁴ Pa. The second cell 13 b filled with SnO₂ is heated to 650 to 925° C., and beam-equivalent pressure of Sn vapor varies depending on the temperature of the second cell 13 b.

As such, the β-Ga₂O₃ based single crystal is epitaxially grown on the Ga₂O₃ based crystal substrate 2 while being doped with Sn and the Ga₂O₃ based crystal film 1 is thereby formed.

Here, a growth temperature and a growth rate of the β-Ga₂O₃ based single crystal are, e.g., respectively 700° C. and 0.01 to 100 μm/h.

The carrier concentration in the Ga₂O₃ based crystal film 1 is 1×10¹⁴ to 1×10²⁰/cm³ and is controlled by the temperature of the second cell 13 b.

Effects of the Embodiment

According to the present embodiment, it is possible to form a highly-conductive Ga₂O₃ based crystal film on a Ga₂O₃ based crystal substrate by epitaxial growth using the MBE method. It is possible to use the formed Ga₂O₃ based crystal film as components of semiconductor elements such as Ga₂O₃ based light-emitting devices or transistors.

The invention is not intended to be limited to the above-mentioned embodiment, and the various kinds of modifications can be implemented without departing from the gist of the invention.

EXAMPLES Example 1

A relation between the temperature of the second cell 13 b filled with SnO₂ powder and the carrier concentration in the Ga₂O₃ crystal film 1 was obtained by experiment.

In the present Example, a substrate formed of a high-resistance β-Ga₂O₃ single crystal doped with 0.25 mol % of Mg was used as the Ga₂O₃ based crystal substrate 2. Meanwhile, a film of a β-Ga₂O₃ single crystal was formed as the Ga₂O₃ based crystal film 1. The principal surface of the Ga₂O₃ based crystal substrate was a (010) plane. The plane orientation of the substrate is not specifically limited but the principal surface of the Ga₂O₃ based crystal substrate is preferably a plane rotated by not less than 50° and not more than 90° with respect to a (100) plane. In other words, on the Ga₂O₃ based substrate, an angle θ (0<θ≦90°) formed between the principal surface and the (100) plane is preferably not less than 50°. Examples of the plane rotated by not less than 50° and not more than 90° with respect the (100) plane include a (010) plane, a (001) plane, a (−201) plane, a (101) plane and a (310) plane.

In addition, during the film formation of the Ga₂O₃ based crystal film 1, partial pressure of the oxygen-based gas was 5×10⁻⁴ Pa, the temperature of the first cell 13 a was 900° C., beam-equivalent pressure of Ga vapor was 2×10⁻⁴ Pa, the growth temperature of the β-Ga₂O₃ single crystal was 700° C. and the growth rate of the β-Ga₂O₃ single crystal was 0.7 μm/h.

Various samples were made at different temperatures of the second cell 13 b filled with SnO₂ in a range of 750 to 850° C. Then, the carrier concentration of each was measured by Hall measurement to obtain a relation between the temperature of the second cell 13 b and the collier concentration in the Ga₂O₃ based crystal film 1.

FIG. 3 is a graph showing a relation between the temperature of the second cell 13 b and the carrier concentration in the Ga₂O₃ based crystal film 1, which was obtained by measurement under the conditions mentioned above. In FIG. 3, the horizontal axis indicates the temperature of the second cell 13 b filled with SnO₂ powder and the vertical axis indicates the carrier concentration in the Ga₂O₃ based crystal film 1. FIG. 3 is a semi-log graph in which the vertical axis is plotted on a logarithmic scale.

As shown in FIG. 3, the measured values on the semi-log graph form a substantially straight line which shows that the carrier concentration in the Ga₂O₃ based crystal film 1 increases with an increase in the temperature of the second cell 13 b.

In addition, when the growth rate of the β-Ga₂O₃ single crystal is multiplied by n (n is a positive real number), the concentration of SnO₂ added to the Ga₂O₃ based crystal film 1 is 1/n and the carrier concentration is also 1/n. Therefore, as shown in FIG. 4, the relation between the temperature of the second cell 13 b and the carrier concentration in the Ga₂O₃ based crystal film 1 at the growth rate of 0.01 to 100 μm/h can be obtained based on the relation at the growth rate of 0.7 μm/h.

Here, 0.01 to 100 μm/h is a growth rate generally used for the β-Ga₂O₃ single crystal. When the growth rate is 0.01 μm/h, for example, the temperature of the first cell 13 a filled with the Ga raw material is 700° C. and partial pressure of the oxygen-based gas is 1×10⁻⁵ Pa. Meanwhile, when the growth rate is 100 μm/h, for example, the temperature of the first cell 13 a is 1200° C. and partial pressure of the oxygen-based gas is 1×10⁻¹ Pa.

The straight lines in FIG. 4 each indicating the relation between temperature of the second cell 13 b and the carrier concentration in the Ga₂O₃ based crystal film 1 are obtained when the growth rates of the β-Ga₂O₃ single crystal are 0.01 μm/h, 0.7 μm/h and 100 μm/h.

It is seen from FIG. 4 that the temperature of the second cell 13 b filled with SnO₂ powder should be 650 to 925° C. in order to obtain a generally-required carrier concentration of 1×10¹⁴ to 1×10²⁰/cm³ under the condition at the growth rate of 0.01 to 100 μm/h.

It was also possible to accurately control the n-type conductivity of the Ga₂O₃ based crystal film in case of using SnO as a Sn raw material even though the temperature range of the second cell 13 b was different from that in the case of using SnO₂. In other words, it is possible to accurately control the n-type conductivity of the Ga₂O₃ based crystal film by using the Sn oxide as the Sn raw material.

On the other hand, if Sn instead of the Sn oxide was loaded as the Sn raw material in the second cell 13 b to form the Ga₂O₃ based crystal film 1, it was not possible to obtain the carrier concentration of not less than 1×10¹⁴/cm³ regardless of the conditions such as the temperature of the second cell 13 b or the growth rate of the β-Ga₂O₃ single crystal.

Meanwhile, when Si was loaded as a conductive impurity in the second cell 13 b instead of the Sn oxide to form the Ga₂O₃ based crystal film 1, it was not possible to control Si vapor pressure depending on the temperature of the second cell 13 b even though the cause is not certain, and it was difficult to highly accurately control the Si amount in the Ga₂O₃ based crystal film 1. FIG. 5 is a graph showing a relation between the temperature of the second cell 13 b filled with Si and the carrier concentration in the Ga₂O₃ based crystal film 1, which was obtained by experiment. The measurement conditions are the same as the case of using the Sn oxide. As shown in FIG. 5, the carrier concentration in the Ga₂O₃ based crystal film 1 varies even at the same temperature of the second cell 13 b and conductivity is not obtained in some cases. Also, when Si oxide (SiO, SiO₂) was used instead of Si, it was not possible to control Si oxide vapor pressure depending on the temperature of the second cell 13 b, and furthermore, the n-type conductivity of the Ga₂O₃ based crystal film 1 was not obtained regardless of the doped amount of Si oxide (even when doped with up to about several mol %).

Example 2

A relation between the temperature of the second cell 13 b filled with SnO₂ powder and the donor concentration in the Ga₂O₃ based crystal film 1 was obtained by experiment.

In the present Example, a substrate formed of an n-type β-Ga₂O₃ single crystal doped with 0.05 mol % of Si was used as the Ga₂O₃ based crystal substrate 2. Meanwhile, a film of a β-Ga₂O₃ single crystal was formed as the Ga₂O₃ based crystal film 1.

The principal surface of the Ga₂O₃ based crystal substrate was a (010) plane. The plane orientation of the substrate is not specifically limited but the principal surface of the Ga₂O₃ based crystal substrate is preferably a plane rotated by not less than 50° and not more than 90° with respect to a (100) plane. In other words, on the Ga₂O₃ based substrate, an angle θ (0<θ≦90 °) formed between the principal surface and the (100) plane is preferably not less than 50°. Examples of the plane rotated by not less than 50° and not more than 90° with respect the (100) plane include a (010) plane, a (001) plane, a (−201) plane, a (101) plane and a (310) plane.

During the film formation of the Ga₂O₃ based crystal film 1, partial pressure of the oxygen-based gas was 5×10⁻⁴ Pa, the temperature of the first cell 13 a was 900° C., beam-equivalent pressure of Ga vapor was 2×10⁻⁴ Pa, the growth temperature of the β-Ga₂O₃ single crystal was 530° C., 570° C. and 600° C. and the growth rate of the β-Ga₂O₃ single crystal was 0.7 μm/h.

Various samples were made at different temperatures of the second cell 13 b filled with SnO₂ in a range of 585 to 820° C. Then, the donor concentration of each was measured by C-V measurement to obtain a relation between the temperature of the second cell 13 b and the donor concentration in the Ga₂O₃ based crystal film 1.

FIG. 6 is a graph showing a relation between the temperature of the second cell 13 b and the miler concentration in the Ga₂O₃ based crystal film 1 (when the growth temperature is set to 530° C., 570° C. and 600°), which was obtained by measurement under the conditions mentioned above. In FIG. 6, the horizontal axis indicates the temperature of the second cell 13 b filled with SnO₂ powder and the vertical axis indicates the donor concentration in the Ga₂O₃ based crystal film 1. FIG. 6 is a semi-log graph in which the vertical axis is plotted on a logarithmic scale.

As shown in FIG. 6, the donor concentration in the Ga₂O₃ based crystal film 1 increases with an increase in the temperature of the second cell 13 b. Here, it was found that the amount of SnO₂ incorporated into an epi film changes with a change in the growth temperature. In detail, the incorporated amount of SnO₂ has a tendency to increase with a decrease in the growth temperature (growth temperature dependence). In this regard, however, the growth temperature dependence decreases at not more than 570° C. In addition, it was also found that the slope of the relation between the SnO₂ cell temperature and the donor concentration at the growth temperature of not more than 570° C. coincides with SnO₂ vapor pressure curve. It was confirmed that, when the growth temperature is lowered to 500° C., the epi surface becomes rough and a film having low crystal quality is grown. Therefore, the growth temperature (substrate temperature) is set between 530° C. and 600° C., preferably, between 530° C. and 570° C. to allow crystal quality to be maintained during growth.

In addition, when the growth rate of the β-Ga₂O₃ single crystal is multiplied by n (n is a positive real number), the concentration of SnO₂ added to the Ga₂O₃ based crystal film 1 is 1/n and the donor concentration is also 1/n. Therefore, as shown in FIG. 7, the relation between the temperature of the second cell 13 b and the donor concentration in the Ga₂O₃ based crystal film 1 at the growth rate of 0.01 to 100 μm/h can be obtained based on the relation at the growth rate of 0.7 μm/h.

Here, 0.01 to 100 μm/h is a growth rate generally used for the β-Ga₂O₃ single crystal. When the growth rate is 0.01 βm/h, for example, the temperature of the first cell 13 a filled with the Ga raw material is 700° C. and partial pressure of the oxygen-based gas is 1×10⁻⁵ Pa. Meanwhile, when the growth rate is 100 μm/h, for example, the temperature of the first cell 13 a is 1200° C. and partial pressure of the oxygen-based gas is 1×10⁻¹ Pa.

FIG. 7 is a graph showing a relation between temperature of the second cell 13 b and the donor concentration in the Ga₂O₃ based crystal film 1 when the respective growth rates of the β-Ga₂O₃ single crystal are 0.01 μm/h, 0.7 μ/h and 100 μm/h (when the growth temperature is set to 570° C.).

It is seen from FIG. 7 that the temperature of the second cell 13 b filled with SnO₂ powder should be 450 to 1080° C. in order to obtain a generally-required donor concentration of 1×10¹⁴ to 1×10²⁰/cm³ under the condition at the growth rate of 0.01 to 100 μm/h.

Although the experiment was conducted using the β-Ga₂O₃ single crystal as the Ga₂O₃ based crystal film 1 in the present Example, substantially the same result is obtained in case of using a β-Ga₂O₃ single crystal in which a Ga site is substituted by Al, etc.

Although the embodiment and examples of the invention have been described above, the invention according to claims is not to be limited to the above-mentioned embodiment and examples. Further, all combinations of the features described in the embodiment and examples are not necessary to solve the problem of the invention.

INDUSTRIAL APPLICABILITY

It is possible to epitaxially grow a Ga₂O₃ based crystal film on a Ga₂O₃ based crystal substrate using an MBE method while controlling the n-type conductivity with high accuracy.

REFERENCE SIGNS LIST

1 Ga₂O₃ based crystal film

2 Ga₂O₃ based crystal substrate

3 MBE apparatus

13 b second cell 

1. A method for producing a Ga₂O₃ based crystal film using a MBE method to form a conductive Ga₂O₃ based crystal film by epitaxial growth, comprising generating Ga vapor and Sn vapor and supplying the Ga vapor and the Sn vapor as a molecular beam to a surface of a Ga₂O₃ based crystal substrate so as to grow a Ga₂O₃ based single crystal film comprising Sn, wherein the Sn vapor is generated by heating a Sn oxide that is filled in a cell of an MBE apparatus.
 2. The method for producing a Ga₂O₃ based crystal film according to claim 1, wherein the Sn oxide comprises SnO₂, and wherein the Sn vapor is generated at a temperature of the cell of 650° C. to 925° C.
 3. The method for producing a Ga₂O₃ based crystal film according to claim 1, wherein the Ga₂O₃ based single crystal film is epitaxially grown at a growth rate of 0.01 to 100 μm/h.
 4. The method for producing a Ga₂O₃ based single crystal film according to claim 1, wherein a carrier concentration of the Ga₂O₃ based crystal film is 1×10¹⁴ to 1×10²⁰/cm³.
 5. The method for producing a Ga₂O₃ based crystal film according to claim 3, wherein a carrier concentration of the Ga₂O₃ based single crystal film is 1×10¹⁴ to 1×10²⁰/cm³.
 6. The method for producing a Ga₂O₃ based crystal film according to claim 1, wherein the Sn oxide comprises SnO₂, and wherein the Sn vapor is generated at a temperature of the cell of 450° C. to 1080° C.
 7. The method for producing a Ga₂O₃ based crystal film according to claim 6, wherein the Ga₂O₃ based single crystal film is epitaxially grown at a growth rate of 0.01 to 100 μm/h.
 8. The method for producing a Ga₂O₃ based crystal film according to claim 6, wherein the Ga₂O₃ based single crystal film is epitaxially grown at a growth temperature of 530° C. to 600° C.
 9. The method for producing a Ga₂O₃ based crystal film according to claim 2, wherein the Ga₂O₃ based single crystal film is epitaxially grown at a growth rate of 0.01 to 100 μm/h.
 10. The method for producing a Ga₂O₃ based crystal film according to claim 2, wherein a carrier concentration of the Ga₂O₃ based single crystal film is 1×10¹⁴ to 1×10²⁰/cm³. 